|Publication number||US6887736 B2|
|Application number||US 10/422,568|
|Publication date||May 3, 2005|
|Filing date||Apr 23, 2003|
|Priority date||Jun 24, 2002|
|Also published as||US7176054, US20040058463, US20050020035|
|Publication number||10422568, 422568, US 6887736 B2, US 6887736B2, US-B2-6887736, US6887736 B2, US6887736B2|
|Inventors||Jeffrey E. Nause, Joseph Owen Maciejewski, Vincente Munne, Shanthi Ganesan|
|Original Assignee||Cermet, Inc.|
|Export Citation||BiBTeX, EndNote, RefMan|
|Patent Citations (47), Non-Patent Citations (13), Referenced by (12), Classifications (21), Legal Events (9)|
|External Links: USPTO, USPTO Assignment, Espacenet|
This patent application is a U.S. nonprovisional application filed pursuant to Title 35, United States Code §§ 100 et seq. and 37 C.F.R. Section 1.53(b) claiming priority under Title 35, United States Code § 119(e) to U.S. provisional application No. 60/391,507 filed Jun. 24, 2002 naming as inventors Jeffrey E. Nause, Joseph Owen Maciejewski, and Vincente Munne as inventors. Both the subject application and its provisional application have been or are under obligation to be assigned to the same entity.
This invention was made pursuant to a Small Business Innovative Research project funded by the U.S. Government as represented by the Office of Naval Research under Contract No. N00014-00-C-0362. The U.S. Government has certain rights in the invention.
1. Field of the Invention
This invention relates to forming compound semiconductor layers using techniques such as metal-oxide chemical vapor deposition (MOCVD) or metal-oxide vapor phase epitaxy (MOVPE). More particularly, this invention relates to methods for forming magnesium, cadmium, and/or zinc oxide crystalline semiconductor layers useful for making electrical and electro-optical devices such as light emitting diodes (LEDs), laser diodes (LDs), field effect transistors (FETs), and photodetectors.
2. Description of the Related Art
For some time there has been interest in producing II-VI compound wide band gap semiconductors to produce green/blue LEDs, LDs and other electrical devices. Historically, attempts to produce these devices have centered around zinc selenide (ZnSe) or gallium nitride (GaN) based technologies. However, these approaches have not been entirely satisfactory due to the short lifetime of light emission that results from defects, and defect migration in these devices.
Recently, because ZnO has a wide direct bandgap of 3.3 electron-Volts (eV) at room temperature and provides a strong emission source of ultraviolet light, ZnO thin films on suitable supporting substrates have been proposed as new materials for LEDs and LDs. Undoped, as well as doped, ZnO films generally show n-type conduction. Impurities such as aluminum and gallium in ZnO films have been studied by Hiramatsu et al. who report activity as n-type donors (Transparent Conduction Zinc Oxide Thin Films Prepared by XeCl Excimer Laser Ablation, J. Vac. Sci. Technol. A 16(2), March/April 1998). Although n-type ZnO films have been available for some time, the growth of p-type ZnO films necessary to build many electrical devices requiring p-n junctions has been much slower in developing.
Minegishi et al. (Growth of P-Type ZnO Films by Chemical Vapor Deposition, Jpn. J. Appl. Phys. Vol. 36 Pt. 2, No. 11A (1997)) recently reported on the growth of nitrogen doped ZnO films by chemical vapor deposition and on the p-type conduction of ZnO films at room temperature. Minegishi et al. disclose the growth of p-type ZnO films on a sapphire substrate by the simultaneous addition of NH3 in carrier hydrogen and excess Zn in source ZnO powder. When a Zn/ZnO ratio of 10 mol % was used, secondary ion mass spectrometry (SIMS) confirmed the incorporation of nitrogen into the ZnO film, although the nitrogen concentration was not precisely confirmed. Although the films prepared by Minegishi et al. using a Zn/ZnO ratio of 10 mol % appear to incorporate a small amount of nitrogen into the ZnO film and convert the conduction to p-type, the resistivity of these films is too high for application in devices such as LEDs or LDs. Also, Minegishi et al. report that the carrier density for the holes is 1.5.×1016 holes/cm3, which is considered to be too low for use in commercial light emitting diodes or laser diodes.
Park et al. in U.S. Pat. No. 5,574,296 disclose a method of producing thin films on substrates by doping IIB-VIA semiconductors with group VA free radicals for use in electromagnetic radiation transducers. Specifically, Park et al. describe ZnSe epitaxial thin films doped with nitrogen or oxygen wherein ZnSe thin layers are grown on a GaAs substrate by molecular beam epitaxy. The doping of nitrogen or oxygen is accomplished through the use of free radical source which is incorporated into the molecular beam epitaxy system. Using nitrogen as the p-type dopant, net acceptor densities up to 4.9×1017 acceptors/cm3 and resistivities less than 15 ohm-cm were measured in the ZeSe film. However, the net acceptor density is too low and the resistivity is too high for use in commercial devices such as LEDs, LDs, and FETs.
White et al in U.S. Pat. No. 6,291,085 disclose a method for producing ZnO films containing p-type dopants, in which the p-type dopant is arsenic and the substrate is gallium arsenide (GaAs). The method of preparation of the film is laser ablation. However, the crystal quality of the films prepared by such a process is inferior and not suitable for device applications.
Although some progress has recently been made in the fabrication of p-type doped ZnO films which can be utilized in the formation of p-n junctions, a need still exists in the industry for ZnO films which contain higher net acceptor concentrations and possess lower resistivity values.
The invented method described herein overcomes the disadvantages noted above with respect to previous techniques for making p-type zinc oxide layers. This method can be used to make relatively high-quality light emitting diodes (LEDs), laser diodes (LDs), field effect transistors (FETs), and photodetectors, and other electrical, electro-optic, or opto-electrical devices.
Broadly stated, a method in accordance with the invention comprises forming a magnesium, cadmium, and/or zinc oxide (Mg1−x−yCdxZnyO; 0≦x<1, 0<y≦1, and x+y=0.1 to 1) II-VI Group compound semiconductor crystal layer with a p-type dopant uniformly incorporated into the layer, with said layer having relatively high crystal quality. The method can be implemented using metalorganic chemical vapor deposition (MOCVD) or metalorganic vapor phase epitaxy (MOVPE) techniques.
In one embodiment, the method for growing a p-type ZnO-based film, optionally with magnesium or cadmium, on a ZnO substrate can comprise cleaning a ZnO substrate. The cleaning can be performed to ensure that a ZnO film can be formed on the ZnO substrate with a reduced number of defects, and will also properly adhere to the substrate. The method can further comprise heating the substrate. The heating of the substrate causes the reaction gases containing magnesium, cadmium, and/or zinc and oxygen, and p-type dopant atoms, to bond and integrate with the substrate to form a relatively crystalline p-type semiconductor layer. The substrate can be heated to a temperature between 250 degrees celsius (C) and about 650 degrees C. The method can further comprise supplying reaction gases into a chamber containing the ZnO substrate. The reaction gases contain zinc and oxygen elements and p-type dopant atoms for forming the p-type ZnO layer. The p-type dopant gas can include one or more atomic elements from Groups IA, IB, VA and/or VB of the periodic table of the elements. For example, such element can include magnesium, cadmium, copper, arsenic, phosphorus, and others. The reaction gases can be admitted into the chamber at flow rates ranging from ten (10) to five-thousand (5000) standard cubic centimeters per minute (sccm). The method can comprise entraining one or more of the reaction gases into a flow of inert gas for delivery to the substrate's surface.
By supplying the reaction gases into the chamber containing the heated substrate, a p-type ZnO-based crystalline semiconductor layer can be grown with the method. The reaction forming the layer can be permitted to continue for sufficient time to produce a ZnO-based layer of a target thickness permitting formation of electrical or electro-optical devices therein.
The p-type ZnO-based layer produced by the disclosed method can be used in LEDs, LDs, FETs, and photodetectors, in which both n-type and p-type materials are required, as a substrate material for lattice matching to other materials in such devices, and/or as a layer for attaching electrical leads, among other possible uses.
Additional objects and advantages of the invention are set forth in the description which follows. The objects and advantages of the invention may be realized and obtained by means of the instrumentalities and combinations particularly pointed out in the appended claims.
The accompanying drawings, which are incorporated herein and constitute a part of the specification, illustrate presently preferred embodiments of the invention, and together with the general description given above and the detailed description of the preferred embodiments given below, serve to explain the principles of the invention.
The invention is now described with reference to the accompanying drawings which constitute a part of this disclosure. In the drawings, like numerals are used to refer to like elements throughout the several views.
The present invention is directed to a method of depositing a ZnO-based II-VI Group compound semiconductor crystal layer on a substrate by the metalorganic chemical vapor deposition or metalorganic vapor phase epitaxy technique. ZnO-based II-VI Group compound semiconductors include zinc oxide (ZnO), magnesium zinc oxide (MgZnO), cadmium zinc oxide (CdZnO), and magnesium cadmium zinc oxide (MgCdZnO). These semiconductors may be represented by the formula:
Mg1−x−yCdxZnyO, in which 0≦x<1, 0<y≦1, and x+y=0.1 to 1.
In the present invention, a reaction gas comprising a first organometallic gas containing zinc, and optionally also magnesium and/or cadmium, and a second gas containing oxygen, are supplied to the surface of the heated substrate surface. The substrate can comprise a bulk ZnO crystal chemically matched to the ZnO layer to be formed. A third dopant gas is also supplied to the heated surface to produce p-type conductivity by introducing dopant atoms into the ZnO layer as it grows. The ZnO-based II-VI Group compound semiconductor crystal grows on the heated substrate surface through the reaction of the first and second gas, and the p-type dopant is uniformly incorporated into the lattice of the crystal as it grows.
The first gas can be at least an organozinc compound such as diethylzinc, dimethylzinc or a mixture thereof. The first gas can further contain an organic compound of a Group III element, other than organogallium compounds. Examples of such an organic compound includes an organomagnesium compound such as bis(cyclopentadienyl)magnesium, bis(methylcyclopentadienyl)magnesium or a mixture thereof, or an organocadmium compound such as dimethylcadmium.
The second gas is oxygen which can react with the first gas to produce a layer of Mg1−x−yCdxZnyO compound on the substrate.
The third gas contains a gaseous p-type dopant source, such as metalorganic or other precursors from Groups IA, IB, VA or VB from the period table of the elements. In the preferred embodiment, p-type dopant sources include bis(tetramethylheptanedianol)copper, arsine, phosphine, or tertiarybutylphosphine to introduce p-type dopant atoms copper, arsenic, and phosphorus, respectively, into the Mg1−x−yCdxZnyO layer.
A shaft 7 is fixed to the center of the lower surface of the susceptor 4, and air-tightly extends outside the chamber 2. The shaft 7 can be connected to and rotated by a drive unit 8, such as an electric motor or servo motor, to rotate the susceptor 4, and hence the carrier plate 3 and substrate 5, during the growth of an Mg1−x−yCdxZnyO layer 9 on the respective substrate 5. The drive unit 8 is connected to the rotation speed controller 9 that regulates the rotation speed imparted by the drive unit 8 to the shaft 7 to maintain a target rotation speed. The target rotation speed can be constant, or alternatively, can be time-varying according to a predetermined rotation-speed-versus-time profile. In some implementations of the method, it can be desirable, for example, to set the rotation speed at a relatively slow rate at the beginning of the process of forming the Mg1−x−yCdxZnyO layer(s) 9, speeding up to be relatively fast toward the end of the process of forming the layer. The controller 10 can be a computer that senses the rotation speed of the shaft 7. For example, the rotation speed can be sensed by a tachometer internal to the drive unit 8, which generates an electric signal indicating the rotation speed on conductive line 11. The rotation speed controller 10 senses the rotation speed, and subtracts it from the target rotation speed internally to the controller 10, to generate an error signal. As previously mentioned, the target rotation speed can be constant in which case it is time-invariant over the entire process. Alternatively, the target rotation speed corresponding to the time elapsed from the start of the timed process can be read from a target rotation speed profile, in which case the target speed for the elapsed time from commencement of the process is read by the controller 10 from its memory, and subtracted from the rotation speed signal, to generate the error signal. The rotation speed controller 10 uses the error signal to adjust the magnitude of the drive current to either speed, slow, or maintain the rotation speed, based on the error signal. The controller 10 supplies the adjusted drive current to the conductive line 12 to the drive unit 8 to drive the shaft 7 to rotate, thereby also rotating the susceptor 4 and carrier plate 3, to rotate the substrate(s) 5.
A heater 13 is arranged to heat the susceptor 4, and hence the carrier plate 3 and substrate 5, to a temperature suitable to grow the desired ZnO-based II-VI Group compound semiconductor crystal layer on the substrate, e.g., about 400 degrees C. or more. In
Injection tubes 24, 25, 26 extend through a wall of chamber 2, and are air-tightly sealed thereto. The injection tubes 24, 25, 26 can be arranged perpendicularly or transversely, to the substrate(s) 5 positioned on the carrier plate 5. Zinc-, cadmium-, and magnesium-containing reaction gases are blown through respective injection tubes 24, 25, 26 perpendicularly to the substrate surface, together with a carrier gas such as argon gas. More specifically, the injection tubes 24, 25, 26 can be connected to respective pressure flow controllers 27, 28, 29. The pressure flow controllers 27, 28, 29 are in turn connected to bubblers 30, 31, 32 containing respective liquid zinc-, cadmium-, and magnesium-organic compounds 33, 34, 35. The bubblers 30, 31, 32 are connected to respective mass flow controllers 36, 37, 38. The mass flow controllers 36, 37, 38 are connected through respective conduits to the tank 39 of carrier gas such as argon. The pressure and mass flow controllers 27, 28, 29, 36, 37, 38 can be electrically connected via lines 40 to the flow controller 41. The flow controller 41 can be implemented as a computer with an input device such as dials or keys permitting a user to set the pressure flow rates for controllers 27, 28, 29 and the mass flow rates for controllers 36, 37, 38. More specifically, the flow controller 41 controls the mass flow controllers 36, 37, 38 to regulate the amount of carrier gas permitted to pass into respective liquid zinc-, cadmium-, and magnesium-organic compounds 33, 34, 35 in the bubblers 27, 28, 29. Through bubbling in liquids 33, 34, 35, the carrier gas flows pick up vaporous zinc-, cadmium-, and magnesium-organic compounds for transport to respective pressure flow controllers 27, 28, 29. The flow controller 41 controls the pressure flow controllers 27, 28, 29 via lines 40 to regulate the pressures at which the respective zinc-, cadmium-, and magnesium-containing gases are introduced into the chamber 2.
To provide oxygen to form the p-type Mg1−x−yCdxZnyO layer(s) 9 on respective substrate(s) 5, injection tube 48 is air-tightly sealed to the wall of chamber 2. The injection tube 42 is connected to a mass flow controller 43 which in turn is connected to a tank 44 of oxygen gas. The injection tube 42 can also be connected to a mass flow controller 45 which is in turn connected to tank 46 of carrier gas such as argon. The mass flow controllers 45 and 46 can be manually-set, or alternatively, can be electronically-controlled with the flow controller 41 via lines 40. The mass flow controllers 43, 45 can be used to generate a flow of carrier gas from tank 44, along with oxygen containing gas from tank 46, enters the chamber 2 through injection tube 42 and is uniformly distributed in a vertical flow towards the substrate 5 via a distribution plate 47. In
An injection tube 48 is provided, and has an outer surface air-tightly sealed to the wall of chamber 2. The injection tube 48 can be used for separate injection of dopant or other reaction gases. The injection tube 48 extends through the dispersion plate 47 and can have a diffusion head 49 defining spaced holes to diffuse carrier and dopant gas received through tube 48. The diffusion head 43 diffuses and directs the carrier and dopant gas against the surfaces of the substrate(s) 5 to form the Mg1−x−yCdxZnyO layer(s) 9 on the respective substrate(s) 5. If the dopant is gaseous, such as a nitrogen- or phosphorus-containing gas, the opposite end of the injection tube 42 can be connected to a mass flow controller 50 that is in turn connected to tank 51 which contains the dopant gas. Alternatively, if the dopant is in liquid form, such as a cadmium- or magnesium-containing volatile liquid, then the injection tube 48 can be connected to a pressure flow controller 52 which is in turn connected to a bubbler 53 containing the dopant-organic compound liquid 54. The bubbler 53 is connected to mass flow controller 55 which is in turn connected to tank 56 of carrier gas such as argon. The controllers 50, 52, 55 can be manually-set, or can be electronically-controller by the flow controller 41 via lines 40. In the case of use of a gaseous dopant, the flow controller 41 regulates flow through the mass flow controller 50 to a regulated level as set by a user. In the case of liquid dopant, the flow controller 41 controls the mass flow controller 55 to permit a regulated amount of carrier gas to pass through controller 55 to bubble in the liquid dopant compound 54 to generate dopant gas that passes at a pressure regulated by controller 41 via pressure flow controller 52 at a desired pressure through injection tube 48 and diffusion head 49 into the chamber 2.
It should be noted that the flow controller 41 can be such as to control the mass flow and pressure flow controllers 27, 28, 29, 36, 37, 38, 43, 45, 50, 52, 55 to produce constant mass and pressure flows, or alternatively, can vary one or more of such flows during the process of growing the p-type Mg1−x−yCdxZnyO layer(s) 9 on the substrate according to a flow-versus-time profile stored in the memory of the controller 41 by a user.
At the lower portion of the chamber 2, an exhaust tube 57 is air-tightly sealed to the chamber 2. Gases inside the chamber 2 can be exhausted using an exhaust pump 58. The exhaust pump 58 can be manually-set to maintain a specified rate of exhausting of gases from the chamber 2. Alternatively, the exhaust pump 58 can be electronically-controlled via a pump controller 59. More specifically, the pump controller 59 receives a pressure signal on line 61 from butterfly valve 60 positioned in the exhaust tube 57. The pressure signal on line 61 indicates the pressure of the gases in the chamber 2. If the pressure of the chamber gases is at or below the target pressure set by a user in the pump controller 59, the pump controller 59 generates the pump signal on line 62 to control the pump 58 to slow the rate of exhausting of gases from the chamber. Conversely, if the sensed pressure is above the target pressure set in the pump controller 59, the pump controller 59 generates the pump control signal to cause the pump 58 to speed the rate of exhausting of gases form the chamber 2 to lower the gas pressure inside the chamber 2. The gas pressure within chamber 2 can thus be maintained at a regulated target pressure.
In a mass production environment, it can be desirable to provide the apparatus 1 with a main controller 61. The main controller 61 is connected to the rotation speed controller 10, the temperature controller 14, the flow controller 41, and the pump controller 59, and can be used to automatically activate or deactivate the such units to execute the process of forming the Mg1−x−yCdxZnyO layer(s) 9 on respective substrate(s) 5.
A substrate 5 can be formed, for example, from a stoichiometric powder of elements comprising the target crystal composition with a gas overpressure using an apparatus and method such as that described in U.S. Pat. No. 5,900,060 issued May 4, 1999 to Jeffrey E. Nause et als., which is incorporated herein by reference. This patent is commonly assigned to the owner of this application, Cermet, Inc., Atlanta, Ga. For example, a ZnO powder can be used in this apparatus and method to produce a ZnO crystal with few or virtually no impurities or defects. The nature of this apparatus and method is such as to produce the crystal from a liquid phase that is contained by a cooler outer solid phase of the same material. After formation, the substrate is cut, polished, and cleaned with a suitable etchant or other chemical agent to produce a flat, defect- and contaminant-free surface on which the Mg1−x−yCdxZnyO layer(s) 9 can be formed.
It is generally preferred that the substrate(s) 5 has crystalline structure with a lattice spacing closely matched to that of the Mg1−x−yCdxZnyO layer(s) 9 to be formed thereon. This helps to lower the number of defects in the layer(s) 9 that would otherwise be caused by lattice mismatch. Thus, ZnO is most preferred compound for use as the substrate(s) 5 because of its close or exact match with the lattice structure of the Mg1−x−yCdxZnyO layer(s) 9 to be formed thereon. However, this does not exclude the possibility of using other substrate compositions, such as sapphire (Al2O3), silicon carbide (SiC), silicon (Si), gallium arsenide (GaAs), and gallium nitride (GaN).
In operation of the apparatus 1, a substrate(s) 5 such as a zinc oxide (ZnO) substrate(s) is placed on the carrier plate 3, which is subsequently placed on the susceptor 4 through port 6. The susceptor 4 is heated with the heater 13 to a temperature of, for example, 250 degrees C. to 1050 degrees C. to heat the substrate 5 to that temperature. The heater 13 can be controlled by temperature controller 14 using a sensed temperature signal from either of temperature sensors 15, 19. The susceptor 4, and hence the carrier plate 3 and substrate 5, is rotated by driving the shaft 7 with drive unit 8. The drive unit 8 controller to rotate the substrate(s) 5 via shaft 7, susceptor 4, and plate 3 at a constant speed or according to a rotation-speed-versus-time profile that varies over time. The dopant, reaction, and carrier gases are supplied in the chamber 2 through respective injection tubes 24, 25, 26, 42, and 48 in a direction perpendicular, or at least transverse, to the substrate 5. The mass and pressure flows of the reaction gases can be set either manually or by using flow controller 41 to generate signals supplied to the controllers 27, 28, 29, 36, 37, 38, 43, 45, 50, 52, 55, to regulate the flows of dopant, reaction, and carrier gases into the chamber 2. Exhaust pump 58 controls the pressure of chamber gases to a target pressure level. This can be done by manual setting of the exhaust pump 58. Alternatively, the chamber pressure can be sensed using the butterfly valve 60 to generate a sensed pressure signal which the pump controller 59 uses to generate the pump control signal to control the pump 58 to maintain the chamber gas pressure to the target pressure level. The chamber pressure can be controlled via the exhaust pump 58 to maintain a pressure of five (5) to fifty (50) torrs of pressure during the layer growth operation. The exhaust pump 58 can control the chamber gas pressure to a constant target pressure throughout the layer growth operation, or alternatively, can vary the gas pressure in the chamber 2 according to a pressure-versus-time profile stored in the memory of the pump controller 59. Spinning of the susceptor 4 and the attached carrier plate 3 and substrate 5 converts the reaction gas flow to one essentially parallel with the surface(s) of substrate(s) 5. The reactants of the reaction gas react with each other to grow the desired ZnO-based II-VI Group compound semiconductor crystal layer on the entire substrate surface.
A p-type ZnO layer was grown on a ZnO substrate by the following steps.
1. Chemically cleaned, n-type ZnO single crystal substrates 5 of (002) crystallographic orientation were placed on the substrate carrier plate 3. This was then loaded onto the reactor susceptor 4 through port 6 and the chamber 2 sealed.
2. The chamber 2 was evacuated using the exhaust pump 58 to less than one-tenth (0.1) torr pressure.
3. A flow of three-thousand (3000) sccm argon and three-hundred (300) sccm oxygen was introduced into the chamber 2 through injection tube 42 via controllers 41, 43, 45, and tanks 44, 46 and the chamber pressure regulated to ten (10) torr with pump 58.
4. Meanwhile, the substrate susceptor temperature was increased to four-hundred (400) degree C. and rotation rate increased to six-hundred (600) revolutions per minute (rpm) in a period of sixty (60) minutes.
5. This state was maintained a period of time until the temperature of the susceptor stabilized at four-hundred (400) degrees C.
6. Diethylzinc vapor was introduced into the chamber at a rate of 1.4×10−4 moles per minute (mol/min) entrained in an argon carrier flow of three-hundred-fifty (350) sccm using controllers 27, 36, 41, bubbler 30, and zinc-containing liquid 33.
7. Meanwhile, tertiarybutylphosphine 54 was introduced into the chamber at a rate of 1.5×10−5 mol/min entrained in an argon flow of three-hundred-fifty (350) sccm using controllers 41, 52, 55, bubbler 53, and tank 56 of argon gas.
8. Meanwhile, the previous three-thousand (3000) sccm argon and three-hundred (300) sccm oxygen flows mentioned were maintained, and the chamber pressure was regulated at ten (10) torr.
9. This state was maintained for one (1) hour during growth of the films 9 on substrates 5.
10. Subsequently, all gas flows were halted except for one-thousand (1000) sccm argon carrier gas from tank 46 via controllers 41, 45, and three-hundred (300) sccm oxygen via controllers 41, 43 and tank 44. The chamber pressure was maintained at ten (10) torr.
11. The state of the system was maintained for sixty (60) minutes after deactivating the heater 13 with the temperature controller 14 while the substrates 5 cooled to near room temperature.
12. All gas flows were halted, and the chamber 2 was evacuated using the exhaust pump 58 to less than one-tenth (0.1) torr.
13. The chamber was then vented with atmosphere, and the substrates were removed.
MgZnO alloy films were grown on ZnO substrates by the following steps.
1. Chemically cleaned, n-type ZnO single crystal substrates 5 of (002) crystallographic orientation were placed on the substrate carrier plate 3. This was then loaded onto the reactor susceptor 4 and the chamber 2 sealed.
2. The chamber 2 was evacuated using the exhaust pump 58 to less than one-tenth (0.1) torr pressure.3. A flow of three-thousand (3000) sccm argon and three-hundred (300) sccm oxygen was introduced into the chamber 2 through injection tube 42 via controllers 41, 43, 45, and tanks 44, 46 and the chamber pressure regulated to ten (10) torr with pump 58.4. Meanwhile, the substrate susceptor temperature was increased to four-hundred (400) degree C. using heater 13, temperature sensor 15 or 19, and temperature controller 14, and rotation rate increased to six-hundred (600) rpm in a period of sixty (60) minutes. This state was maintained a period of time until the temperature of the susceptor 4 stabilized at four-hundred (400) degree C.
3. Diethylzinc vapor was introduced into the chamber at a rate of 2.9×10−5 mol/min entrained in an argon carrier flow of three-hundred-fifty (350) sccm using controllers 27, 36, 41, bubbler 30, and zinc-containing liquid 33.
4. Meanwhile, bis(methylcyclopentadienyl)magnesium vapor was introduced into the chamber 2 via controllers 29, 38, 41, bubbler 32, magnesium-containing liquid 35, and tank 39 of argon carrier gas 41, at a rate of 5.8×10−6 mol/min entrained in an argon carrier flow of three-hundred-fifty (350) sccm.
5. Meanwhile, the previous three-thousand (3000) sccm argon and three-hundred (300) sccm oxygen flows mentioned were maintained with units 42-47, and the chamber pressure was regulated at ten (10) torr with exhaust pump 58.
6. This state was maintained for ninety (90) minutes during growth of the films.
7. Subsequently, all gas flows were halted except for one-thousand (1000) sccm argon carrier gas from tank 46 via controllers 41, 45 and three-hundred (300) sccm oxygen via controllers 41, 43 and tank 44. The chamber pressure was maintained at ten (10) torr by exhaust pump 58.
8. The state of the system was maintained for sixty (60) minutes after deactivating the heater 13 using the temperature controller 14 while the substrates cooled to near room temperature.
9. All gas flows were halted, and the chamber 2 was evacuated using the exhaust pump 58 to less than one-tenth (0.1) torr.
10. The chamber 2 was then vented with atmosphere, and the substrates 5 were removed through port 6.
Due to the fact that the substrate and Mg1−x−yCdxZnyO layer grown thereon are relatively pure and are closely matched in their crystalline lattice spacing, as well as the activation of a large number of dopant atoms in the layer, net acceptor concentration within the layer is relatively high and resistivity is relatively low as compared to layers produced with previous methods. For example, it is possible to produce layers with net acceptor concentrations of at least 1017/cm3 and resistivities of at least one-tenth (0.1) Ohm-cm. Hence, the methods disclosed herein are useful for generating relatively high-performance, commercially-viable devices such as LEDs, LDs, and FETs.
Although the methods of the invention have been described herein with reference to specific embodiments and examples, it is not necessarily intended to limit the scope of the invention to the specific embodiments and examples disclosed. Thus, in addition to claiming the subject matter literally defined in the appended claims, all modifications, alterations, and equivalents to which the applicant is entitled by law, are herein expressly reserved by the following claims.
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|U.S. Classification||438/104, 438/509, 438/505, 438/503|
|International Classification||C23C16/458, C30B25/02, C23C16/40, C23C16/44, C23C16/455|
|Cooperative Classification||C30B25/02, C23C16/45565, C23C16/40, C23C16/45574, C23C16/407, C23C16/4584|
|European Classification||C30B25/02, C23C16/458D2B, C23C16/455K10, C23C16/40, C23C16/455K2, C23C16/40L|
|Apr 23, 2003||AS||Assignment|
|Aug 16, 2005||CC||Certificate of correction|
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